CN1714160A - Method for making an abrasion resistant steel plate and plate obtained - Google Patents
Method for making an abrasion resistant steel plate and plate obtained Download PDFInfo
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- CN1714160A CN1714160A CNA2003801036477A CN200380103647A CN1714160A CN 1714160 A CN1714160 A CN 1714160A CN A2003801036477 A CNA2003801036477 A CN A2003801036477A CN 200380103647 A CN200380103647 A CN 200380103647A CN 1714160 A CN1714160 A CN 1714160A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 68
- 239000010959 steel Substances 0.000 title claims abstract description 68
- 238000000034 method Methods 0.000 title claims abstract description 21
- 238000005299 abrasion Methods 0.000 title abstract description 8
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 24
- 238000001816 cooling Methods 0.000 claims abstract description 22
- 239000000126 substance Substances 0.000 claims abstract description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 229910052711 selenium Inorganic materials 0.000 claims abstract description 5
- 229910052714 tellurium Inorganic materials 0.000 claims abstract description 5
- 239000010936 titanium Substances 0.000 claims description 54
- 239000000463 material Substances 0.000 claims description 35
- 229910000734 martensite Inorganic materials 0.000 claims description 20
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 18
- 238000005096 rolling process Methods 0.000 claims description 18
- 229910001566 austenite Inorganic materials 0.000 claims description 17
- 230000000717 retained effect Effects 0.000 claims description 14
- 238000010791 quenching Methods 0.000 claims description 10
- 229910001563 bainite Inorganic materials 0.000 claims description 8
- 238000002360 preparation method Methods 0.000 claims description 8
- 239000010949 copper Substances 0.000 claims description 7
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 230000000171 quenching effect Effects 0.000 claims description 3
- 239000002893 slag Substances 0.000 claims description 3
- 238000003856 thermoforming Methods 0.000 claims description 2
- 229910052720 vanadium Inorganic materials 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract 2
- 229910052745 lead Inorganic materials 0.000 abstract 1
- 229910052799 carbon Inorganic materials 0.000 description 21
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 20
- 229910052726 zirconium Inorganic materials 0.000 description 15
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 12
- 230000000694 effects Effects 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 9
- 239000011572 manganese Substances 0.000 description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 8
- 239000011651 chromium Substances 0.000 description 6
- 239000010955 niobium Substances 0.000 description 6
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 5
- 239000005864 Sulphur Substances 0.000 description 5
- 238000006243 chemical reaction Methods 0.000 description 5
- 229910052757 nitrogen Inorganic materials 0.000 description 5
- 229910052796 boron Inorganic materials 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 150000004767 nitrides Chemical class 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 230000008021 deposition Effects 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000011733 molybdenum Substances 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 229910052721 tungsten Inorganic materials 0.000 description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- 208000034189 Sclerosis Diseases 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 1
- 208000027418 Wounds and injury Diseases 0.000 description 1
- 229910026551 ZrC Inorganic materials 0.000 description 1
- OTCHGXYCWNXDOA-UHFFFAOYSA-N [C].[Zr] Chemical compound [C].[Zr] OTCHGXYCWNXDOA-UHFFFAOYSA-N 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 208000014674 injury Diseases 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000008188 pellet Substances 0.000 description 1
- 229920001296 polysiloxane Polymers 0.000 description 1
- 239000010453 quartz Substances 0.000 description 1
- 150000003346 selenoethers Chemical class 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- XSOKHXFFCGXDJZ-UHFFFAOYSA-N telluride(2-) Chemical compound [Te-2] XSOKHXFFCGXDJZ-UHFFFAOYSA-N 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000007669 thermal treatment Methods 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
Abstract
The invention concerns a method for making an abrasion resistant steel plate having a chemical composition comprising: 0.35 % </= C </= 0.8 %, 0 % </= Si </= 2 %; 0 % </= AI </= 2 %; 0.35 % </= Si + AI </= 2 %; 0 % </= Mn </= 2.5 %; 0 % </= Ni </= 5 %; 0 % </= Cr </= 5 %; 0 % </= Mo </= 0.050; 0 % </= W </= 1 %; 0,1 % </= Mo +W/2 </= 0.5 %; 0 % </= B </= 0.02 %; 0 % </= Ti </= 2 %; 0 % </= Zr </= 4 %; 0.05 % </= Ti + Zr/2 </= 2 %; 0 % </= S </= 0.15 %; N </= 0,03; optionally 0 % to 1.5 % of Cu; optionally Nb, Ta or V with Nb/2 + Ta/4 + V </= 0.5 %; optionally less than 0.1 % of Se, Te, Ca, Bi or Pb; the rest being iron and impurities; the composition satisfying: 0.1 % < C* = C - Ti/4 - Zr/8 + 7xN/8 </= 0.55 % and 1.05xMn + 0.54xNi +0.5OxCr + 0.3x(Mo + W/2)<1/2> + K > 1.8, with K = 0.5 if B >/= 0.0005 % and K = 0 if B < 0.0005 % and Ti+Zr/2-7xN/2 >/= 0.05 %; hardening after austenitization while cooling at a speed > 0,5 DEG C/s between a temperature > AC3 and ranging between T = 800 - 270xC* - 9OxMn -37xNi - 70XCr - 83x(Mo + W/2) and T-50 DEG C; then at a core speed Vr < 1150XEP<-1.7> between T and 100 DEG C, (ep = plate thickness in mm); cooling down to room temperature. The invention also concerns the resulting plate.
Description
Technical field
The present invention relates to wear-resisting steel and preparation method thereof.
Background technology
Known wear-resisting steel have high hardness (400 to 500Brinell) usually, have martensitic structure and contain 0.12% to 0.3% carbon.It has been generally acknowledged that,, need only improve the hardness of steel, but can destroy other characteristic of steel, for example welding characteristic or bending forming characteristic like this in order to improve wear resistance.Therefore, in order to obtain the steel that not only have extraordinary wear resistance but also have favorable applicability, people begin to attempt other method except that increasing hardness.
In order to improve the wear resistance of steel, EP 0527276 and US 5,393,0.015% to 1.5% titanium is added in 358 suggestions in steel, to form thick titanium carbide, contain 0.05% to 0.45% carbon in the described steel, be not higher than 1% silicon, be not higher than 2% manganese, be not higher than 2% copper, be not higher than 10% nickel, be not higher than 3% chromium and be not higher than 3% molybdenum, boron, niobium and vanadium.Described steel are quenched so that it has martensitic structure, and the appearance of thick titanium carbide makes the wear resistance of steel be improved.Yet when described steel was cast stick, the improvement of described wear resistance was restricted, because under the effect of wearing and tearing stress (abrasive stress), carbide can be separated, thereby can't play a role.And the existence of thick titanium carbide has influenced the ductility of steel in these steel.Therefore, the steel plate that is got by described steel is difficult to finish rolling and bending, thereby has limited their application.
Summary of the invention
The objective of the invention is and will overcome the above-mentioned defective of prior art by a kind of attrition resistant steel plate is provided, described steel plate has the surface of good planeness, and is keeping under the constant situation of other characteristic, and the wear resistance of described steel plate is better than known steel.
For this reason, the present invention relates to a kind of particularly method of sheet material of attrition resistant steel workpiece for preparing, the chemical constitution of described workpiece comprises by weight:
0.35％≤C≤0.8％；
0％≤Si≤2％；
0％≤Al≤2％；
0.35％≤Si+Al≤2％；
0％≤Mn≤2.5％；
0％≤Ni≤5％；
0％≤Cr≤5％；
0％≤Mo≤0.050％；
0％≤W≤1.00％；
0.1％≤Mo+W/2≤0.50％；
0％≤Cu≤1.5％；
0％≤B≤0.02％；
0％≤Ti≤2％；
0％≤Zr≤4％；
0.05％≤Ti+Zr/2≤2％；
0％≤S≤0.15％；
N＜0.03％；
-optional at least a the element that is selected from Nb, Ta and V, their content satisfies Nb/2+Ta/4+V≤0.5%;
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, its content is less than or equals 0.1%;
The impurity that produces in the iron of-surplus and the preparation process;
Described chemical constitution also satisfies following relation:
0.10%≤C
*≤ 0.55%, C wherein
*=C-Ti/4-Zr/8+7 * N/8 and
Ti+Zr/2-7 * N/2 〉=0.05% and
1.05 * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2)
1/2+ K＞1.8, more preferably greater than 2, wherein, if B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0;
According to described method, in the thermoforming heat of for example rolling heat, described workpiece or sheet material are carried out the hot quenching processing, perhaps after austenitizing, implement quench treatment by reheat in stove, described quench treatment comprises:
-cool off described workpiece or sheet material with average rate of cooling greater than 0.5 ℃/s, with temperature from being higher than AC
3Temperature reduce to T=800-270 * C
*-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2) and between T-50 ℃, wherein temperature is with a ℃ expression, C
*, Mn, Cr, Mo and W content represent with weight %;
-subsequently with less than 1150 * ep
-1.7(in ℃/s) and average core rate of cooling (the core cooling rate) Vr that is higher than 0.1 ℃/s cool off described workpiece or sheet material, temperature is reduced to 100 ℃ from T, wherein ep is the thickness of slab in mm;
-then described workpiece or sheet material are cooled to room temperature, and choose wantonly and carry out finish rolling processing (planishing).
After quenching, choose wantonly and carry out temper under the temperature that is being lower than 350 ℃, and preferably carry out temper being lower than under 250 ℃ the temperature.
The invention still further relates to a kind of workpiece that is made by aforesaid method, particularly sheet material, described steel comprise 5% to 20% retained austenite, and surplus is martensitic structure or martensite/bainite structure and carbide.When described workpiece was sheet material, its thickness can be 2mm to 150mm, and its surface finish is shown with deviation card and is less than or equal to 12mm/m, preferably less than 5mm/m.
When carbon content satisfied 0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.2%, steel hardness was between 280HB to 450HB.
When carbon content satisfied 0.2%＜C-Ti/4-Zr/8+7 * N/8≤0.3%, steel hardness was between 380HB to 550HB.
When carbon content satisfied 0.3%＜C-Ti/4-Zr/8+7 * N/8≤0.5%, steel hardness was between 450HB to 650HB.
Describe the present invention in detail below by embodiment, but these are not limitation of the present invention.
In order to prepare sheet material of the present invention, the steel that preparation has following chemical constitution in weight %:
-0.35% to 0.8% carbon, preferred carbon content are higher than 0.45% or be higher than 0.5%; 0% to 2% Ti, 0% to 4% Zr, the content of Ti and Zr satisfies 0.05%≤Ti+Zr/2≤2%.Carbon is mainly used in and forms sufficiently rigid martensitic structure, and is used to form the carbide of Ti and/or Zr.The total amount of Ti+Zr/2 must be higher than 0.05%, preferably be higher than 0.10%, more preferably be higher than 0.3%, more preferably be higher than 0.5% again, draw the minimum of formed carbide thus, but it must be lower than 2%, preferably smaller or equal to 0.9%, because be higher than this level, the toughness of steel and suitability can be affected.
The Al of the Si and 0% (or trace) of-0% (or trace) to 2% to 2%, the total amount of Si+Al is preferably greater than 0.5%, more preferably greater than 0.7% between 0.35% to 2%.These elements are not only reductor, also have the effect of the formation that promotes metastable retained austenite, and described austenite contains a large amount of carbon, and it follows bigger expansion when changing into martensitic structure, and this can promote the set of titanium carbide.
The Cr of the Mn of-0% (or trace) to 2% or 2.5%, 0% (or trace) Ni and 0% (or trace) to 4% or 5% to 4% or 5% is so that obtain enough quenchability (quenchability) and adjust various mechanical characteristics or use properties.Nickel is for raising toughness particularly advantageous, but nickel is comparatively expensive.Chromium also can form thin carbide in martensite or bainite structure.
The Mo of-0% (or trace) to 0.50%.This element can improve quenchability and form thin sclerosis carbide in martensite or bainite structure, particularly by the deposition that causes owing to auto-tempering in process of cooling.The content of Mo need not to surpass 0.50% can reach the ideal effect, particularly for the deposition of sclerosis carbide.Can use the tungsten of twice consumption partly or entirely to replace molybdenum.Yet in fact this replacement is unfavorable, does not bring more benefit and price more expensive because compare tungsten with molybdenum.
-optional 0% to 1.5% copper.Copper can bring additional hardening effect under the situation that does not influence weldability.Copper content is higher than at 1.5% o'clock, and effect does not significantly improve, and causes hot rolling difficulty and unnecessary cost to increase on the contrary.
-0% to 0.02% B.The optional boron that adds improves quenchability.In order to reach required effect, the content of boron preferably is higher than 0.0005%, more preferably is higher than 0.001%, but need not basically to surpass 0.01%.
-be no more than 0.15% sulphur.As resistates, the content of element sulphur is limited in 0.005% or lower usually, but in order to improve workability, also can initiatively carry doctor positive content.Should be pointed out that to exist under the situation of sulphur that for fear of encountering difficulties, the content of manganese must be higher than 7 times of sulphur content in thermal distortion.
-optional at least a the element that is selected among Nb, Ta and the V, their content satisfies Nb/2+Ta/4+V≤0.5%, so that form thicker carbide, thereby improves wear resistance.But the effect of the carbide that is formed by these elements is effective not as the carbide that formed by titanium or zirconium, therefore, and optional these elements of interpolation, and limit their consumption.
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, wherein every kind of content all is less than 0.1%.These elements are used to improve workability.Should be pointed out that when containing Se and/or Te in the steel, consider the content of sulphur, the content of manganese will guarantee to form the selenide or the telluride of manganese.
The impurity that produces in the iron of-surplus and the preparation process.Described impurity especially comprises nitrogen, and nitrogen content depends on the preparation method, but is no more than 0.03% usually.The nitrogen element can form nitride in titanium or zirconium reaction, and formed nitride necessarily can not be too thick, in order to avoid infringement toughness.In order to prevent to form thick nitride; can in molten steel, add titanium and zirconium very lentamente; for example oxidation phase (slag that for example contains the oxide compound of titanium or zirconium) can be contacted with the oxidation molten steel, then with deoxidation of molten steel, so that titanium or zirconium slowly are diffused into the molten steel mutually from oxidation.
In addition, in order to obtain satisfied characteristic, the content of carbon, titanium, zirconium and nitrogen element must satisfy: 0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.55%,
C-Ti/4-Zr/8+7 * N/8=C wherein
*, C
*Be illustrated in the carbide free carbon content afterwards of titanium deposition and zirconium, consider the formation of the nitride of titanium and zirconium.Described free carbon content must be higher than 0.1%, and is preferably greater than or equals 0.22% so that martensite has minimum hardness, but free carbon content be higher than at 0.55% o'clock can grievous injury toughness and suitability.
Consider the thickness of the sheet material that will produce, must further select to have enough quenchability to guarantee steel to above-mentioned chemical constitution.For this reason, described chemical constitution also must satisfy following relation:
Quench index (Quench)=1.05 * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2)
1/2+ K＞1.8 are preferably greater than 2, if wherein B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0.
Should be pointed out that in order to promote the formation of retained austenite when quench index was between 1.8 and 2.0, the content of preferred silicon was higher than 0.5%.
In addition, in order to guarantee the enough content of carbide, the content of Ti, Zr and N preferably satisfies: Ti+Zr/2-7 * N/2 〉=0.05%, and more preferably greater than 0.1%, again more preferably greater than 0.3%.
At last, in order to obtain good wear resistance, the microtexture of described steel mainly is made of the mixed structure of martensite or bainite structure or two kinds of structures, and comprises 5% to 20% austenitic structure; Described structure also comprises thick titanium or zirconium carbide or niobium, tantalum or the vanadium carbide that at high temperature forms.The inventor finds that separating out too early of described thick carbide can the thick carbide of infringement improve the effect of wear resistance, metastable austenitic existence then can prevent separating out too early of carbide, because these austenites that influence of wear phenomenon are converted to new martensite.Because metastable austenite often is accompanied by expansion to new martensitic conversion, the described conversion that occurs in the wearing and tearing subgrades (abraded sub-layer) helps stoping separating out of carbide, thereby improves wearing and tearing patience.
In addition, because the hardness of described steel is higher and wherein also have the titanium carbide of embrittlement, need reduce the finish rolling operation as much as possible.Given this, the inventor finds the rate of temperature fall by fully slowing down between the bainite/martensite zone of transformation, can reduce the residual set of product, thereby can reduce the finish rolling operation.The inventor finds by with less than 1150 * ep
-1.7(wherein ep is in the thickness of slab of mm, rate of cooling with ℃/s represents) rate of cooling Vr cool the temperature to and be lower than T=800-270 * C
*-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2), (with a ℃ expression) promoted the generation of the residual austenite of remarkable ratio on the one hand, also reduced the unrelieved stress that is caused by phase transformation on the other hand.
In order to prepare very flat sheet material, prepare described steel and it is cast into sheet material or bar with good wear resistance.Described sheet material or rod hot rolling with preparation sheet material, are heat-treated this sheet material then, so that without further finish rolling or the structure and the surface of good planeness that obtain to wish by limited finish rolling.Described thermal treatment can directly be pined for carrying out also can carrying out subsequently in rolling, chooses wantonly after cold finish rolling or middle temperature finish rolling.
In order to carry out described heat treatment operation:
-described steel are heated above AC
3Point is so that convert it into austenitic structure completely;
-then,, be cooled to and be equal to or slightly less than temperature T (than low about 50 ℃ of T), described temperature T=800-270 * C its average rate of cooling with the critical conversion rate that is higher than bainite
*-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2), (with a ℃ expression);
-subsequently, with less than 1150 * ep
-1.7(to obtain desirable structure) and the average core rate of cooling Vr that is higher than 0.1 ℃/s (to obtain enough hardness) cool off described sheet material, and temperature is reduced to about 100 ℃ from said temperature (promptly about T to than T-50 ℃ between);
-then described sheet material is cooled to room temperature, preferred low rate of cooling but and nonessential.
In addition, can be less than or equal under 350 ℃ the temperature, preferably, carry out stress relief and handle being less than or equal under 250 ℃ the temperature.
Can make a kind of sheet material by this way, its thickness can be between 2mm to 150mm, and without finish rolling or only through it has excellent surface finish under the situation of appropriate finish rolling, described surface finish is expressed as less than 12mm/m with deviation (deflection).The hardness of described sheet material is between 280HB to 650HB.This hardness depends on the content C of free carbon basically
*=C-Ti/4-Zr/8+7 * N/8.
Along with free carbon content C
*Increase, the firmness level raises, particularly:
If a) 0.1%≤C
*≤ 0.2%, then hardness is greatly about between the 280HB to 450HB;
B) if 0.2%＜C
*≤ 0.3%, then hardness is greatly about between the 380HB to 550HB;
C) if 0.3%＜C
*≤ 0.5%, then hardness is greatly about between the 450HB to 650HB.
Because hardness is free carbon content C
*Function, can adopt different titaniums or zirconium content to obtain identical hardness.Under the identical situation of hardness, along with the increase of the content of titanium or zirconium, wear resistance gets a promotion.Similarly, when the content of titanium or zirconium is identical, along with the increase wear resistance of hardness also improves.In addition, along with the minimizing of free carbon content, the use of described steel becomes easier, but for identical free carbon content, the ductility of steel improves along with the minimizing of titanium content.By considering above-mentioned factor, can select carbon content and titanium or zirconium content to make the steel that are fit to each Application Areas.
According to the difference of hardness, steel for example can be used for following purposes:
-between 280HB to 450HB: the tank car of shovel, truck or dump car, hurricane shielding, hopper and concrete mold;
-between 380HB to 550HB: the scraper plate and the screen cloth grid of the shield of bump shredder, blade, clamshell-type dump bucket;
-between 450HB to 650HB: the reinforcing member under the shielding slab of cartridge type shredder, the reinforcing member of hopper, the primary blades, cut wiper blade shielding (cut-water blade shields), major cutting edge (leading edges).
For instance, investigate according to steel plate A to G of the present invention and prior art steel plate H to J.The chemical constitution of steel plate is (with 10
-3Weight % represents), the content and the abrasion resistance index Rus of hardness, retained austenite structure list in the table 1.
Table 1
| ??C | ??Si | ??Al | ??Mn | ??Ni | ??Cr | ??Mo | ??W | ??Ti | ??B | ??N | ??HB | The % austenite | ??Rus | |
| ??A | ??360 | ??850 | ??50 | ??1300 | ??500 | ??700 | ??100 | ??500 | ??400 | ??2 | ??6 | ??460 | ??10 | ??1.42 |
| ??B | ??640 | ??850 | ??50 | ??400 | ??1500 | ??700 | ??110 | ??450 | ??620 | ??3 | ??7 | ??555 | ??14 | ??2.72 |
| ??C | ??590 | ??520 | ??570 | ??550 | ??320 | ??1850 | ??470 | ??- | ??540 | ??- | ??7 | ??570 | ??12 | ??2.24 |
| ??D | ??705 | ??460 | ??630 | ??1090 | ??280 | ??2450 | ??430 | ??100 | ??825 | ??- | ??7 | ??580 | ??13 | ??3.14 |
| ??E | ??690 | ??370 | ??25 | ??740 | ??310 | ??2100 | ??460 | ??- | ??795 | ??- | ??6 | ??605 | ??10 | ??2.83 |
| ??F | ??350 | ??810 | ??30 | ??1200 | ??270 | ??1350 | ??380 | ??160 | ??2 | ??6 | ??510 | ??8 | ??1.32 | |
| ??G | ??390 | ??790 | ??35 | ??1210 | ??250 | ??1340 | ??390 | ??405 | ??3 | ??6 | ??495 | ??11 | ??1.77 | |
| ??H | ??340 | ??380 | ??30 | ??1260 | ??470 | ??820 | ??370 | ??- | ??410 | ??3 | ??6 | ??475 | ??1 | ??0.86 |
| ??I | ??315 | ??330 | ??25 | ??1230 | ??180 | ??1360 | ??395 | ??165 | ??2 | ??6 | ??515 | ??2 | ??0.7 | |
| ??J | ??367 | ??315 | ??30 | ??1215 | ??210 | ??1375 | ??405 | ??430 | ??2 | ??5 | ??500 | ??2 | ??1.01 |
Rotation prism-shaped sample in the container that the graded quartz pellet is housed, abrasion resistance index Rus changes with the variation of the antilogarithm of the weight loss of this sample.
The thickness of these sheet materials is 30mm, and the sheet material corresponding to steel A to G is quenched after 900 ℃ are carried out austenitizing according to the present invention.
After austenitizing, cooling conditions is as follows:
-for the sheet material of making by steel B and D: according to the inventive method, cool the temperature on the said temperature T with the average rate of cooling of 0.7 ℃/s, the average rate of cooling with 0.13 ℃/s cools the temperature under the T then;
-for the sheet material of making by steel A, C, E, F and G: according to the inventive method, cool the temperature on the said temperature T with the average rate of cooling of 6 ℃/s, the average rate of cooling with 1.4 ℃/s cools the temperature under the T then;
-in contrast the sheet material of making by steel H, I and J: carry out austenitizing at 900 ℃, then the average rate of cooling with 20 ℃/s cools the temperature on the said temperature T, and the average rate of cooling with 12 ℃/s cools the temperature under the T then.
Sheet material according to the present invention has martensite/bainite structure, wherein contains 5% to 20% retained austenite, and contrast sheet material then has martensitic structure completely, that is to say that contained retained austenite is no more than 2 to 3% martensitic structure.These sheet materials all contain carbide.
To comparison shows that of wear resistance, under similar hardness and titanium content, the abrasion resistance index Rus of sheet material of the present invention on average exceeds 0.5 than the abrasion resistance index Rus of prior art sheet material.Especially, the contrast table of diverse embodiment A of structure and H (content of retained austenite is 10% among the A, then all is martensite among the H) is understood the probability that occurs retained austenite in the structure.The difference that should be pointed out that retained austenite content is because the difference of heat treatment operation is because the difference of silicone content on the other hand on the one hand.
Find also that in addition under the identical situation of other factors, and the situation of carbonaceous deposits in the matrix that does not contain retained austenite compared, the coexistence of titanium carbide and retained austenite among the present invention causes titanium carbide obviously higher to the contribution of wear resistance.Therefore, therefore identical titanium content difference (identical TiC content difference, carbon is still excessive) caused wear resistance increase in F steel and G steel (steel of the present invention) is different from obviously that caused wear resistance increases in I steel and J steel.For F steel and G steel, increase to 0.46 by the caused abrasion resistance index Rus of 0.245% Ti, and for I steel and J steel, being increased by the caused abrasion resistance index Rus of 0.265% Ti only is 0.31.
Above-mentioned phenomenon can be owing to the improve of matrix around when containing retained austenite in the matrix to the jam-packed effect (squeezing effect) of titanium carbide, these retained austenites can change into hard martensitic structure under the effect of wearing and tearing stress, and described conversion process is accompanied by bigger expansion.
In addition, less than 10mm/m, and be 15mm/m without the cooling after strain of the steel plate of the present invention of finish rolling for the described cooling after strain of H steel plate.
In actual applications, can can provide product without finish rolling according to the present invention, perhaps carry out finish rolling, but described finish rolling is more or less freely and only need use less pressure, because the distortion of product of the present invention itself is less in order to satisfy stricter surface finish to require (for example 5mm/m).
Claims (20)
1, a kind of method for preparing attrition resistant steel workpiece such as sheet material, the chemical constitution of described workpiece comprises by weight:
0.35％≤C≤0.8％；
0％≤Si≤2％；
0％≤Al≤2％；
0.35％≤Si+Al≤2％；
0％≤Mn≤2.5％；
0％≤Ni≤5％；
0％≤Cr≤5％；
0％≤Mo≤0.50％；
0％≤W≤1.00％；
0.1％≤Mo+W/2≤0.50％；
0％≤B≤0.02％；
0％≤Ti≤2％；
0％≤Zr≤4％；
0.05％≤Ti+Zr/2≤2％；
0％≤S≤0.15％；
N＜0.03％；
-optional 0% to 1.5% copper;
-optional at least a the element that is selected among Nb, Ta and the V, their content satisfies Nb/2+Ta/4+V≤0.5%;
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, its content is less than or equals 0.1%;
The impurity that produces in the iron of-surplus and the preparation process;
Described chemical constitution also satisfies following relation:
0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.55% and
Ti+Zr/2-7 * N/2 〉=0.05% and
1.05 1/2+K＞1.8 of * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2), wherein, if B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0;
According to described method, in the thermoforming heat of for example rolling heat, described sheet material is carried out hot quenching and handle, perhaps after austenitizing, implement quench treatment by reheat in stove, described quench treatment comprises:
-cool off described workpiece or sheet material with average rate of cooling greater than 0.5 ℃/s, with temperature from being higher than AC
3Temperature reduce to T=800-270 * C
*-90 * Mn-37 * Ni-70 * Cr-83 * (Mo+W/2) and between T-50 ℃, wherein C
*=C-Ti/4-Zr/8+7 * N/8;
-subsequently with less than 1150 * ep
-1.7And the average core rate of cooling Vr that is higher than 0.1 ℃/s cools off described workpiece or sheet material, and temperature is reduced to 100 ℃ from T, and wherein ep is the thickness of slab in mm;
-then described workpiece or sheet material are cooled to room temperature, and choose wantonly and carry out the finish rolling processing.
2, according to the method for claim 1, it is characterized in that:
1.05×Mn+0.54×Ni+0.50×Cr+0.3×(Mo+W/2)
1/2+K＞2。
3, according to the method for claim 1 or 2, it is characterized in that: C＞0.45%.
4, according to the arbitrary described method of claim 1-3, it is characterized in that:
Si+Al＞0.5％。
5, according to the arbitrary described method of claim 1-4, it is characterized in that:
Ti+Zr/2＞0.10％。
6, according to the arbitrary described method of claim 1-5, it is characterized in that:
Ti+Zr/2＞0.30％。
7, according to the arbitrary described method of claim 1-6, it is characterized in that:
C
*≥0.22％。
8,, it is characterized in that again carrying out temper being less than or equal under 350 ℃ the temperature according to the arbitrary described method of claim 1-7.
9,, it is characterized in that molten steel being contacted with the titaniferous slag, so that the titanium in the slag slowly is diffused in the molten steel in order in steel, to add titanium according to the arbitrary described method of claim 1-8.
10, a kind of attrition resistant steel workpiece such as sheet material, the chemical constitution of described workpiece comprises by weight:
0.35％≤C≤0.8％；
0％≤Si≤2％；
0％≤Al≤2％；
0.35％≤Si+Al≤2％；
0％≤Mn≤2.5％；
0％≤Ni≤5％；
0％≤Cr≤5％；
0％≤Mo≤0.50％；
0％≤W≤1.00％；
0.1％≤Mo+W/2≤0.50％；
0％≤B≤0.02％；
0％≤Ti≤2％；
0％≤Zr≤4％；
0.05％≤Ti+Zr/2≤2％；
0％≤S≤0.15％；
N＜0.03％；
-optional 0% to 1.5% copper;
-optional at least a the element that is selected among Nb, Ta and the V, their content satisfies Nb/2+Ta/4+V≤0.5%;
-optional at least a the element that is selected among Se, Te, Ca, Bi and the Pb, its content is less than or equals 0.1%;
The impurity that produces in the iron of-surplus and the preparation process;
Described chemical constitution also satisfies following relation:
0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.55% and
Ti+Zr/2-7 * N/2 〉=0.05% and
1.05 * Mn+0.54 * Ni+0.50 * Cr+0.3 * (Mo+W/2)
1/2+ K＞1.8, wherein, if B 〉=0.0005%, then K=0.5; If B＜0.0005%, then K=0;
Its surface finish is shown less than 12mm/m with deviation card, and described steel have martensitic structure or martensite/bainite structure, also comprises 5% to 20% retained austenite and carbide in the described structure.
11, according to the workpiece of claim 10, it is characterized in that:
1.05×Mn+0.54×Ni+0.50×Cr+0.3×(Mo+W/2)
1/2+K＞2。
12, according to the workpiece of claim 10 or 11, it is characterized in that: C＞0.45%.
13, according to the arbitrary described workpiece of claim 10-12, it is characterized in that:
Si+Al＞0.5％。
14, according to the arbitrary described workpiece of claim 10-13, it is characterized in that:
Ti+Zr/2＞0.10％。
15, according to the arbitrary described workpiece of claim 10-14, it is characterized in that:
Ti+Zr/2＞0.30％。
16, according to the arbitrary described workpiece of claim 10-15, it is characterized in that:
C
*≥0.22％。
17,, it is characterized in that it is that thickness is the sheet material of 2mm to 150mm, and its surface finish is shown less than 12mm/m with deviation card according to the arbitrary described workpiece of claim 10-16.
18, according to the arbitrary described workpiece of claim 10-17, it is characterized in that its hardness between 280HB to 450HB, and 0.1%≤C-Ti/4-Zr/8+7 * N/8≤0.2%.
19, according to the arbitrary described workpiece of claim 10-17, it is characterized in that its hardness between 380HB to 550HB, and 0.2%＜C-Ti/4-Zr/8+7 * N/8≤0.3%.
20, according to the arbitrary described workpiece of claim 10-17, it is characterized in that its hardness between 450HB to 650HB, and 0.3%＜C-Ti/4-Zr/8+7 * N/8≤0.5%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FR02/14424 | 2002-11-19 | ||
| FR0214424A FR2847270B1 (en) | 2002-11-19 | 2002-11-19 | METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET |
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|---|---|
| CN1714160A true CN1714160A (en) | 2005-12-28 |
| CN100350061C CN100350061C (en) | 2007-11-21 |
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|---|---|
| US (3) | US7459041B2 (en) |
| EP (1) | EP1563104B1 (en) |
| JP (1) | JP4535877B2 (en) |
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| AR (1) | AR042071A1 (en) |
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| DE (1) | DE60322092D1 (en) |
| ES (1) | ES2309377T3 (en) |
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| RU (1) | RU2327802C2 (en) |
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